CN107190128A - The manufacture method of 780MPa grades of cold-rolled biphase steels of high-yield strength - Google Patents

The manufacture method of 780MPa grades of cold-rolled biphase steels of high-yield strength Download PDF

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Publication number
CN107190128A
CN107190128A CN201710419254.0A CN201710419254A CN107190128A CN 107190128 A CN107190128 A CN 107190128A CN 201710419254 A CN201710419254 A CN 201710419254A CN 107190128 A CN107190128 A CN 107190128A
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temperature
cold
yield strength
steel
manufacture method
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CN201710419254.0A
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Chinese (zh)
Inventor
潘利波
林承江
李立军
周文强
胡宽辉
王小鹏
杜小峰
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Wuhan Iron and Steel Co Ltd
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Wuhan Iron and Steel Co Ltd
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Priority to CN201710419254.0A priority Critical patent/CN107190128A/en
Publication of CN107190128A publication Critical patent/CN107190128A/en
Pending legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The invention discloses a kind of manufacture method of high-yield strength 780MPa grades of cold-rolled biphase steels, it is characterised in that comprises the following steps：Hot rolling, finish to gauge, batch, it is cold rolling, annealing, slow cooling, rapid cooling, overaging, smooth, nine steps, wherein, hot rolling heating-up temperature is 1270~1330 DEG C, 860~900 DEG C of finishing temperature, 610~650 DEG C of coiling temperature, cold rolling reduction ratio 55~72%, 810~830 DEG C of annealing process annealing temperature, 620~640 DEG C of slow cooling section end temp, rapid cooling 280~310 DEG C of end temp of section, 260~300 DEG C of overaging temperature, smooth elongation percentage 0.3%~0.6%.The present invention has higher yield strength and tensile strength, the good beneficial effect of reaming flange.

Description

The manufacture method of 780MPa grades of cold-rolled biphase steels of high-yield strength
Technical field
The present invention relates to the manufacture method of cold-rolled biphase steel, specifically a kind of high-yield strength 780MPa grades of cold-rolled biphase steels Manufacture method.
Background technology
Based on phase transformation strengthening, it is advanced that the cold-rolled biphase steel (DP steel) of matrix is made up of ferrite and martensite Model in high-strength steel.It has the spy such as low yield strength ratio, high initial manufacture hardening rate and good intensity and ductility cooperation Point, it is widely used by domestic and international automobile factory.Ultralight steel car body project research shows, use of the dual phase steel on future automobile vehicle body Amount is up to 80%, with good market application foreground.In recent years, the Main way of dual phase steel research and development is further to improve cold Roll the strong plasticity level and formability of dual phase steel, particularly each cold rolling DP590-DP1180 of intensity rank elongation and should be hardened Change Index n Value, while carrying out new technology development and improvement in terms of chemical composition, production technology and microscopic structure.
Traditionally, because dual phase steel is mainly used to make automotive body structure part or safety member, these parts Deform in most cases not extremely complex, and intensity is not too high, therefore shaping gets up less problematic.But as automobile is set Meter continuous change continued to develop with light-weighted, increasing structural member while requiring to possess certain drawing feature, Also possess stronger flange feature, and this kind of structural member intensity requirement also more and more higher, largely require that the strength of materials reaches More than 780MPa grades, the requirement of intensity can not be met using 590MPa grades and following dual phase steel, using common low yield strength ratio The preferable 780MPa grades of dual phase steel of plasticity, which can not meet flange, to be asked, and often flange cracking occurs in part.Accordingly, it would be desirable to be directed to The part of this kind of feature, optimizes the reaming performance of material, to meet the requirement of auto vendor.
The content of the invention
The invention aims to solve the deficiency that above-mentioned background technology is present, proposition is a kind of to have higher surrender strong Degree and tensile strength, the manufacture method of the good 780MPa grades of cold-rolled biphase steels of high-yield strength of reaming flange.
In order to realize the above object a kind of manufacturer for high-yield strength 780MPa grades of cold-rolled biphase steels that the present invention is provided Method, it is characterised in that comprise the following steps：Hot rolling, finish to gauge, batch, it is cold rolling, annealing, slow cooling, rapid cooling, overaging, smooth, nine Individual step, wherein, hot rolling heating-up temperature is 1270~1330 DEG C, 860~900 DEG C of finishing temperature, 610~650 DEG C of coiling temperature, Cold rolling reduction ratio 55~72%, 810~830 DEG C of annealing process annealing temperature, 620~640 DEG C of slow cooling section end temp, rapid cooling section 280~310 DEG C of end temp, 260~300 DEG C of overaging temperature, smooth elongation percentage 0.3%~0.6%.
As the preferred scheme of the present invention, the chemical composition of the steel is C：0.07~0.09%；Si：0.25~ 0.35%；Mn：1.75~1.85%；P：Less than 0.012%；；Cr：0.2~0.3%；Alt：0.02~0.07%；Nb：0.015 ~0.025%；Constraint element S：Less than 0.005%；N：Less than 0.005%, surplus is Fe
Beneficial effects of the present invention：The cold rolling two-phase of 780MPa level high-yield strengths produced using the technical scheme Steel, because by suitable chemical composition and controlling of production process, products obtained therefrom has higher yield strength and good reaming Flange performance.Therefore when using the production body of a motor car high-strength structure part, gained part strength is high, flange quality It is good, good light weight effect can be played to body structure, with significant Social benefit and economic benefit.
Embodiment
Embodiment：A kind of manufacture method of high-yield strength 780MPa grades of cold-rolled biphase steels, comprises the following steps：Hot rolling, Finish to gauge, batch, cold rolling, annealing, slow cooling, rapid cooling, overaging, smooth, nine steps, wherein, hot rolling heating-up temperature be 1270~ 1330 DEG C, 860~900 DEG C of finishing temperature, 610~650 DEG C of coiling temperature, cold rolling reduction ratio 55~72%, annealing process annealing 810~830 DEG C of temperature, 620~640 DEG C of slow cooling section end temp, rapid cooling 280~310 DEG C of end temp of section, overaging temperature 260~300 DEG C, smooth elongation percentage 0.3%~0.6%.The chemical composition of steel is C：0.07~0.09%；Si：0.25~ 0.35%；Mn：1.75~1.85%；P：Less than 0.012%；；Cr：0.2~0.3%；Alt：0.02~0.07%；Nb：0.015 ~0.025%；Constraint element S：Less than 0.005%；N：Less than 0.005%, surplus is Fe.
Compared with prior art, the advantage of this technology is：
(1) Design of Chemical Composition：
Carbon can significantly improve the intensity of steel, and particularly in dual phase steel, contents of the C in martensite directly affects martensite Intensity, and then the tensile strength of steel is influenceed, but the carbon content in steel is too high totally unfavorable to forming property, can also deteriorate material Welding performance.Therefore its content is limited to 0.07~0.09% scope.
Element silicon has catharsis in dual phase steel to ferrite matrix, suppresses the formation of carbide, while promoting C from iron Ferritic matrix spreads to austenite, but excessive Si elements can cause iron scale indivisible etc. in hot rolling production process asks Topic.So, its content is limited to 0.25~0.35% scope.
Manganese element can play a part of expanding austenitic area, and improve the intensity of steel, but higher manganese content can be to steel-making Adversely affected with casting process, it is contemplated that steel needs the intensity rank reached, and its content is limited into 1.75~1.85% Scope.
Phosphorus belongs to control element in the present invention, and its content requirement is low, it is considered to its combined influence to Steel Properties, is limited It is scheduled on less than 0.012%.
Aluminium is added as deoxidier in the present invention, it is ensured that the pure but excessive aluminium content of molten steel can form oxygen Change aluminium to be mingled with.The Alt contents considered in steel are controlled 0.02~0.07%.
Chromium can play a part of expanding austenitic area, reduce the temperature of austenitizing, ensure the forming amount of martensite, Consider the performance impact to steel, its content range is controlled 0.2~0.3%.
Niobium is that annealing recrystallization process can be effectively hindered in dual phase steel, the tissue of fining ferrite, so as to improve iron Ferritic matrix hardness and intensity, realize high-yield strength, and niobium can also make the diffusion path of C and alloying element shorten, be conducive to C With the diffusion of alloying element.But niobium is relatively valuable, it is considered to cost of alloy, its content is limited to 0.015~0.025%.
Sulphur belongs to control element in steel of the present invention, and its content is more low better, therefore by sulfur content control in steel 0.005% Below.
Nitrogen is harmful element in steel, influences the forming property of steel.Therefore by the control of its content below 0.005%.
The present invention is designed using relatively reasonable cost of alloy, both ensure that steel plate had the intensity of superelevation, and in turn ensure that Steel plate has good flange performance.
The technical program is produced using C-Si-Mn-Cr-Nb chemical composition System Design, its chemical analysis weight percent Than for：C：0.07~0.09%；Si：0.25~0.35%；Mn：1.75~1.85%；P：Less than 0.012%；；Cr：0.2~ 0.3%；Alt：0.02~0.07%；Nb：0.015~0.025%；Constraint element S：Less than 0.005%；N：Less than 0.005%, Surplus is Fe.
(2) production technology
Slab heating temperature, finish to gauge in course of hot rolling, the performance important to dual phase steel such as batch；Cold-rolling process Middle influence final performance is cold rolling reduction ratio, and big cold rolling reduction ratio is conducive to the uniformity of subsequent product tissue and performance； The annealing temperature of annealing process is crucial for dual phase steel, it is necessary to control to anneal in two-phase section, so that follow-up cooled Ferrite and martensite duplex structure are obtained in journey.Cooling velocity is determined by several temperature control points in annealing process, Such as slow cooling section outlet temperature and rapid cooling section outlet temperature, austenite, which is transformed into martensite, needs cooling velocity to reach certain requirement. In addition, the overaging section of annealing process can play stable effect to martensite, the tensile strength for controlling dual phase steel is extremely closed It is important.
Therefore the production technology of the product design is that hot rolling heating-up temperature is 1270~1330 DEG C, finishing temperature 860~900 DEG C, 610~650 DEG C of coiling temperature, cold rolling reduction ratio 55~72%, 810~830 DEG C of annealing process annealing temperature, slow cooling section knot 620~640 DEG C of Shu Wendu, rapid cooling 280~310 DEG C of end temp of section, 260~300 DEG C of overaging temperature, smooth elongation percentage 0.3%~0.6%.
(3) product microstructure and mechanical property
Product microstructure is that ferrite adds a certain proportion of martensite duplex structure.Product has higher yield strength And tensile strength, reaming flange is good.500~580MPa of yield strength, tensile strength is higher than 780MPa, elongation (A50mm) no Less than 10%, hole expansibility improves more than 30% than common 780MPa grades of DP steel.
The above described is only a preferred embodiment of the present invention, not doing any formal to the structure of the present invention Limitation.Any simple modification, equivalent variations and modification that every technical spirit according to the present invention is made to above example, In the range of still falling within technical scheme.
Table 1 is the actual smelting composition of product of each embodiment, and table 2 is the technological parameter of each embodiment, and table 3 is each for the present invention The behavior pattern of embodiment.
Embodiment C Si Mn P S Alt Nb Cr N
1 0.08 0.30 1.8 0.009 0.003 0.04 0.02 0.25 0.0022
2 0.070 0.35 1.75 0.011 0.0049 0.02 0.023 0.30 0.003
3 0.085 0.25 1.78 0.010 0.005 0.03 0.025 0.28 0.0049
4 0.09 0.28 1.83 0.008 0.0038 0.05 0.018 0.21 0.0025
5 0.078 0.32 1.85 0.011 0.0045 0.07 0.015 0.20 0.0024
Table 1
Table 2
Table 3

Claims (2)

1. a kind of manufacture method of high-yield strength 780MPa grades of cold-rolled biphase steels, it is characterised in that comprise the following steps：Heat Roll, finish to gauge, batch, cold rolling, annealing, slow cooling, rapid cooling, overaging, smooth, nine steps, wherein, hot rolling heating-up temperature be 1270 ~1330 DEG C, 860~900 DEG C of finishing temperature, 610~650 DEG C of coiling temperature, cold rolling reduction ratio 55~72%, annealing process is moved back Fiery 810~830 DEG C of temperature, 620~640 DEG C of slow cooling section end temp, rapid cooling 280~310 DEG C of end temp of section, overaging temperature 260~300 DEG C, smooth elongation percentage 0.3%~0.6%.
2. the manufacture method of high-yield strength 780MPa grades of cold-rolled biphase steels according to claim 1, it is characterised in that：Institute The chemical composition for stating steel is C：0.07~0.09%；Si：0.25~0.35%；Mn：1.75~1.85%；P：0.012% with Under；；Cr：0.2~0.3%；Alt：0.02~0.07%；Nb：0.015~0.025%；Constraint element S：Less than 0.005%；N： Less than 0.005%, surplus is Fe.
CN201710419254.0A 2017-06-06 2017-06-06 The manufacture method of 780MPa grades of cold-rolled biphase steels of high-yield strength Pending CN107190128A (en)

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN110004362A (en) * 2019-04-01 2019-07-12 山东钢铁集团日照有限公司 A kind of production method improving cold rolling DP780 steel yield tensile ratio and reaming performance
CN110016615A (en) * 2019-04-26 2019-07-16 本钢板材股份有限公司 A kind of cold-rolled biphase steel DP780 and its Flexible Production method
CN108950405B (en) * 2018-08-14 2020-02-18 武汉钢铁有限公司 800 MPa-grade multi-phase steel with good flanging performance and production method thereof

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004068050A (en) * 2002-08-02 2004-03-04 Sumitomo Metal Ind Ltd High tensile strength cold rolled steel sheet and its manufacturing method
CN101153369A (en) * 2006-09-27 2008-04-02 宝山钢铁股份有限公司 Cold-rolled high-strength diphasic strip steel and manufacturing process thereof
CN102605240A (en) * 2011-12-09 2012-07-25 首钢总公司 High-strength and high-plasticity dual-phase steel and manufacturing method thereof
CN103060703A (en) * 2013-01-22 2013-04-24 宝山钢铁股份有限公司 780MPa grade cold rolling biphase strip steel and manufacturing method thereof
CN104109814A (en) * 2014-08-08 2014-10-22 鞍钢蒂森克虏伯汽车钢有限公司 Cold-rolled hot-galvanized dual-phase steel plate with flanging property and manufacturing method thereof
CN105543674A (en) * 2015-12-18 2016-05-04 东北大学 Method for manufacturing cold-rolled ultrahigh-strength dual-phase steel with high local forming performance

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004068050A (en) * 2002-08-02 2004-03-04 Sumitomo Metal Ind Ltd High tensile strength cold rolled steel sheet and its manufacturing method
CN101153369A (en) * 2006-09-27 2008-04-02 宝山钢铁股份有限公司 Cold-rolled high-strength diphasic strip steel and manufacturing process thereof
CN102605240A (en) * 2011-12-09 2012-07-25 首钢总公司 High-strength and high-plasticity dual-phase steel and manufacturing method thereof
CN103060703A (en) * 2013-01-22 2013-04-24 宝山钢铁股份有限公司 780MPa grade cold rolling biphase strip steel and manufacturing method thereof
CN104109814A (en) * 2014-08-08 2014-10-22 鞍钢蒂森克虏伯汽车钢有限公司 Cold-rolled hot-galvanized dual-phase steel plate with flanging property and manufacturing method thereof
CN105543674A (en) * 2015-12-18 2016-05-04 东北大学 Method for manufacturing cold-rolled ultrahigh-strength dual-phase steel with high local forming performance

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108950405B (en) * 2018-08-14 2020-02-18 武汉钢铁有限公司 800 MPa-grade multi-phase steel with good flanging performance and production method thereof
CN110004362A (en) * 2019-04-01 2019-07-12 山东钢铁集团日照有限公司 A kind of production method improving cold rolling DP780 steel yield tensile ratio and reaming performance
CN110016615A (en) * 2019-04-26 2019-07-16 本钢板材股份有限公司 A kind of cold-rolled biphase steel DP780 and its Flexible Production method

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